US9587297B2 - Ferritic stainless steel excellent in corrosion resistance and conductivity and method for manufacturing the same, separator of proton-exchange membrane fuel cell and proton-exchange membrane fuel cell - Google Patents

Ferritic stainless steel excellent in corrosion resistance and conductivity and method for manufacturing the same, separator of proton-exchange membrane fuel cell and proton-exchange membrane fuel cell Download PDF

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US9587297B2
US9587297B2 US13/876,234 US201113876234A US9587297B2 US 9587297 B2 US9587297 B2 US 9587297B2 US 201113876234 A US201113876234 A US 201113876234A US 9587297 B2 US9587297 B2 US 9587297B2
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Tomohiro Ishii
Shin Ishikawa
Takumi Ujiro
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/28—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by cold-rolling, e.g. Steckel cold mill
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
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    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C23G1/086—Iron or steel solutions containing HF
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/02—Details
    • H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
    • H01M8/0204—Non-porous and characterised by the material
    • H01M8/0206—Metals or alloys
    • H01M8/0208—Alloys
    • H01M8/021—Alloys based on iron
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/10—Fuel cells with solid electrolytes
    • H01M2008/1095—Fuel cells with polymeric electrolytes
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/30—Hydrogen technology
    • Y02E60/50—Fuel cells
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
    • Y02P70/50—Manufacturing or production processes characterised by the final manufactured product
    • Y02P70/56—

Definitions

  • the present invention relates to ferritic stainless steel excellent in corrosion resistance and conductivity as it is, despite not having undergone a surface treatment such as plating and to a manufacturing method of the same.
  • Fuel cells which are excellent in power generation efficiency and which do not emit CO 2 are being developed from the viewpoint of global environment conservation.
  • Fuel cells are classified into types such as a phosphoric-acid fuel cell, a solid oxide fuel cell and a proton-exchange membrane fuel cell on the basis of kind of electrolyte which is used for the fuel cell.
  • proton-exchange membrane fuel cells are applied to stationary type electric generators for household use, onboard power supplies of fuel-cell electric vehicles and so forth, because proton-exchange membrane fuel cells can work at a low temperature of 100° C. or lower, can be started up in a short time and can be suitably reduced in size.
  • Patent document 1 discloses stainless steel to be used for a separator of a proton-exchange membrane fuel cell having a chemical composition containing, by mass %, C ⁇ 0.03%, N ⁇ 0.03%, 20% ⁇ Cr ⁇ 45% and 0.1% ⁇ Mo ⁇ 5.0%, the atomic ratio of Cr to Fe Cr/Fe in a passivation film being 1 or more.
  • Patent document 2 discloses a separator for a proton-exchange membrane fuel cell, which is made of stainless steel, having a chemical composition containing, by mass %, 15% ⁇ Cr ⁇ 40% and 1% ⁇ Mo ⁇ 5%, and Mo/(Mo+Cr+Fe) in terms of atomic ratios comprising Mo, Cr and Fe in a passivation film being 0.3 or less and 1.5 times or more the value of Mo/(Mo+Cr+Fe) in a substrate.
  • Patent document 3 discloses a separator for a proton-exchange membrane fuel cell having a chemical composition containing, by mass %, 16% ⁇ Cr ⁇ 40% and 1% ⁇ Mo ⁇ 5%, micro pits whose diameters are 0.01 ⁇ m or more and 1 ⁇ m or less being formed in the entire region of the surface and the atomic ratio of Cr to Fe Cr/Fe in a passivation film being 4 or more.
  • Patent document 1 Japanese Unexamined Patent Application Publication No. 2004-149920
  • Patent document 2 Japanese Unexamined Patent Application Publication No. 2006-253107
  • Patent document 3 Japanese Unexamined Patent Application Publication No. 2008-91225
  • an object of the present invention is to provide ferritic stainless steel excellent in corrosion resistance and conductivity that can be ideally used for a separator of a proton-exchange membrane fuel cell.
  • Said proton-exchange membrane fuel cell has low contact resistance and makes it possible to achieve corrosion resistance in a potential range in which Cr exhibits transpassive dissolution.
  • the present inventors conducted investigations on the influences of a chemical composition of a ferritic stainless steel, and immersing the ferritic stainless steel into acid, on a contact resistance and on a transpassive dissolution.
  • a chemical composition of a ferritic stainless steel by specifying the chemical composition and by reforming a passivation film by using an immersion treatment in a solution mainly containing a specified acid, it is possible to achieve not only low contact resistance but also corrosion resistance in a potential range in which Cr exhibits the transpassive dissolution.
  • the present invention has been completed on the basis of the knowledge described above and provides the following items (1) through (13).
  • a ferritic stainless steel excellent in corrosion resistance and conductivity the stainless steel having a chemical composition containing, by mass %, C: 0.001% or more and 0.05% or less, Si: 0.001% or more and 0.5% or less, Mn: 0.001% or more and 1.0% or less, Al: 0.001% or more and 0.5% or less, N: 0.001% or more and 0.05% or less, Cr; 17% or and 23% or less, Mo: 0.1% or less and the balance being Fe and inevitable impurities, and the stainless steel having a passivation film on the surface of the stainless steel, said film is obtained by immersing the stainless steel in a solution for an immersion treatment, said solution mainly contains hydrofluoric acid or a liquid mixture of hydrofluoric acid and nitric acid, and in said solution the relationship represented by the following expression (1) is satisfied, where [HF] denotes the concentration of hydrofluoric acid (mass %) and [HNO 3 ] denotes the concentration of nitric acid (mass %). [HF]
  • a separator of a proton-exchange membrane fuel cell consisting of the ferritic stainless steel according to any one of items (1) to (5).
  • a method for manufacturing ferritic stainless steel including subjecting a cold-rolled stainless steel sheet or an annealed cold-rolled stainless steel sheet having the chemical composition according to any one of items (1), (4) or (5) to an immersion treatment in a solution for the immersion treatment, said solution mainly contains hydrofluoric acid or a liquid mixture of hydrofluoric acid and nitric acid and said solution is adjusted so that the relationship between the concentration of hydrofluoric acid (mass %) [HF] and the concentration of nitric acid (mass %) [HNO 3 ] becomes [HF] ⁇ [HNO 3 ] ([HNO3] includes zero).
  • ferritic stainless steel that can be ideally used for a separator of a proton-exchange membrane fuel cell suppressing an increase in contact resistance for a long time of power generation, ensuring corrosion resistance in a potential range in which Cr exhibits transpassive dissolution despite not having undergone a surface treatment such as plating.
  • FIG. 1 is a graph illustrating an influence of the concentration of hydrofluoric acid and the concentration of nitric acid on contact resistance after immersion in a liquid mixture of hydrofluoric acid and nitric acid has been performed.
  • FIG. 2 is a graph illustrating an influence of Cr content and Mo content in steel on contact resistance after a endurance test has been performed in a potential range in which Cr exhibits transpassive dissolution.
  • the ferritic stainless steel according to the present invention has a specified chemical composition and a passivation film on the surface of the stainless steel, said film is obtained by immersing the stainless steel in a solution for an immersion treatment, said solution mainly contains hydrofluoric acid or a liquid mixture of hydrofluoric acid and nitric acid and in said solution the relationship represented by the following expression (1) is satisfied, where [HF] denotes the concentration of hydrofluoric acid and [HNO 3 ] denotes the concentration of nitric acid. [HF] ⁇ [HNO 3 ] (1)
  • concentration of hydrofluoric acid [HF] and the concentration of nitric acid [HNO 3 ] in the present invention are given in units of mass %.
  • the present inventors conducted various investigations on a contact resistance by immersing ferritic stainless steel having various chemical compositions in various kinds of acid such as hydrochloric acid, sulfuric acid and a liquid mixture of hydrofluoric acid and nitric acid, and, as a result, found that a film, which is obtained by reforming a passivation film by immersing ferritic stainless steel having a specific chemical composition in a solution for an immersion treatment, in said solution the relationship [HF] ⁇ [HNO 3 ] is satisfied as described above, reduces contact resistance down to a value which is ideal for a separator of a proton-exchange membrane fuel cell.
  • acid such as hydrochloric acid, sulfuric acid and a liquid mixture of hydrofluoric acid and nitric acid
  • Example 1 The knowledge described above was derived from Example 1 which will be described below. That is to say, in reference to FIG. 1 in which Example 1 is summarized, the following results were derived:
  • contact resistance is further decreased down to the value of less than 10 m ⁇ cm 2 by immersing ferritic stainless steel in a solution for an immersion treatment in which the relationship represented by the expression (2) described above, that is, [HF] ⁇ 2.5[HNO 3 ] is satisfied.
  • an essential requirement for ensuring contact resistance of ferritic stainless steel which can be used as a separator of a proton-exchange membrane fuel cell is that the ferritic stainless steel have a passivation film which is formed by immersing the ferritic stainless steel in a solution for an immersion treatment in which the expression (1) described above is satisfied, and a preferable requirement is that the ferritic stainless steel have a passivation film which is formed by immersing the ferritic stainless steel in a solution for an immersion treatment, in said solution the expression (2) described above is satisfied.
  • a solution for an immersion treatment mainly contains hydrofluoric acid or a liquid mixture of hydrofluoric acid and nitric acid
  • hydrochloric acid, sulfuric acid, organic acid, an accelerator, an inhibitor and so forth may be contained in the solution for an immersion treatment in addition to hydrofluoric acid and nitric acid.
  • the contents of hydrochloric acid, sulfuric acid and organic acid be 20 mass % or less each and 50 mass % or less in total.
  • an accelerator and an inhibitor it is preferable that their contents be 3.0 volume % or less each.
  • the chemical composition of stainless steel for a separator of a proton-exchange membrane fuel cell according to the present invention will be described hereafter.
  • the stainless steel according to the present invention is ferritic stainless steel having a chemical composition containing the chemical components in the ranges as described below, respectively.
  • “%” shall denote “mass %”, unless otherwise noted.
  • Cr is an important element which determines the corrosion resistance of stainless steel, and, in the case where a potential is in a range of a passive state, the higher the Cr content, the better the corrosion resistance.
  • a practical service environment of a separator of a fuel cell is usually in a passive state, where high corrosion resistance is required. In the case where a Cr content is less than 17%, sufficient corrosion resistance cannot be ensured and there is an increase in contact resistance due to a power generation for a long time.
  • the present inventors conducted a constant potential test in a transpassive state (for example, in an environment of being in a sulfuric acid solution having a pH value of 3 and at an applied potential of 1.0 V (vs.SHE)) and estimated contact resistance after the constant potential test had been performed, and, as a result, the tendency that transpassive dissolution was accelerated along with an increase in a Cr content in steel was confirmed. That is to say, in the case where a potential is increased up to a transpassive state, Cr dissolves as hexavalent ions, and thus, transpassive dissolution is accelerated along with an increase in a Cr content.
  • Acceleration of transpassive dissolution fosters growth of a passivation film or formation of a corrosion product, which results in an increase in contact resistance.
  • dissolution of a Cr ion results in a decrease in the performance of an electrolyte membrane of a fuel cell. Acceleration of transpassive dissolution described above is significant in the case where the Cr content is more than 23%. Therefore, the Cr content in steel is set to be 17% or more and 23% or less, preferably 20% or more and 22% or less.
  • Mo is generally a chemical element which increases corrosion resistance of stainless steel. It is preferable that Mo content be 0.005% or more in order to realize this effect. However, comparing in constant Cr content, it has been found that an increase in contact resistance after a constant potential test has been performed is more significant in the case of stainless steel having a Mo content of more than 0.1%, in comparison to the case of stainless steel having no Mo content.
  • C is a chemical element which is inevitably contained in stainless steel and effectively increases the strength of steel by solute strengthening. This effect cannot be realized with a C content of less than 0.001%.
  • an increase in the C content accelerates precipitation of Cr carbide and locally decreases the Cr content of a matrix metal surrounding the Cr carbide, which results in a decrease in the corrosion resistance of stainless steel. This tendency is significant in the case where C content is more than 0.05%. Therefore, C content is set to be 0.001% or more and 0.05% or less, preferably 0.002% or more and 0.04% or less.
  • Si 0.001% or More and 0.5% or Less
  • Si is a chemical element which is effective for deoxidation, and this effect is realized with a Si content of 0.001% or more.
  • an excessive Si content makes fabrication of a separator difficult due to a decrease in workability. This tendency is significant in the case where the Si content is more than 0.5%. Therefore, the Si content is set to be 0.001% or more and 0.5% or less, preferably 0.002% or more and 0.4% or less.
  • Mn 0.001% or More and 1.0% or Less
  • Mn is a chemical element which is inevitably contained in steel and effective for strengthening steel. This effect cannot be realized with a Mn content of less than 0.001%. However, since Mn causes precipitation of MnS which becomes a source of corrosion, an excessive Mn content causes a decrease in corrosion resistance. In addition, it was confirmed that there is a tendency of an increase in contact resistance due to the existence of Mn in a passivation film. These kinds of negative influences are significant in the case where the Mn content is more than 1.0%. Therefore, the Mn content is set to be 0.001% or more and 1.0% or less, preferably 0.002% or more and 0.8% or less.
  • Al is a chemical element which is effective for deoxidation, and this effect is realized with an Al content of 0.001% or more.
  • the excessive Al content of more than 0.5% causes problems not only in fabrication of a separator due to a decrease in workability but also in descaling by pickling in the case where an oxidized film is formed, which results in a decrease in manufacturability. Therefore, the Al content is set to be 0.001% or more and 0.5% or less, preferably 0.002% or more and 0.4% or less.
  • N is, as well as C, a chemical element which is inevitably contained in steel and effective for increasing the strength of steel by solute strengthening. Moreover, N is also effective for increasing corrosion resistance by forming a solid solution in steel. These effects cannot be realized with a N content of less than 0.001%. On the other hand, excessive N content of more than 0.05% cause a decrease in corrosion resistance of stainless steel by precipitating Cr nitride. Therefore, N content is set to be 0.001% or more and 0.05% or less, preferably 0.002% or 0.04%.
  • Ti is a chemical element suppresses a decrease in corrosion resistance by preventing a precipitation of Cr carbonitride, since Ti combines preferentially with C and N.
  • an excessive Ti content of more than 0.6% causes not only a decrease in workability but also an increase in the particle size of Ti carbonitride, which results in the formation of surface defects. Therefore, in the case where Ti is contained, the Ti content is set to be 0.6% or less. It is preferable that the Ti content be 0.01% or more and 0.6% or less, because the effect described above is realized more effectively with a Ti content of 0.01% or more.
  • the Ti content is more preferably 0.05% or more and 0.4% or less.
  • Nb is a chemical element which suppresses a decrease in corrosion resistance by preventing a precipitation of Cr carbonitride, since Nb combines preferentially with C and N.
  • an excessive Nb content of more than 0.6% causes an increase in warm strength and hot rolling load, which results in difficulty in manufacturing. Therefore, in the case where Nb is contained, the Nb content is set to be 0.6% or less. It is preferable that the Nb content be 0.01% or more and 0.6% or less, because the effect described above is realized more effectively with a Nb content of 0.01% or more.
  • the Nb content is more preferably 0.05% or more and 0.4% or less.
  • Zr is a chemical element which suppresses a decrease in corrosion resistance by preventing a precipitation of Cr carbonitride, since Zr combines preferentially with C and N.
  • an excessive Zr content of more than 0.6% causes a decrease in workability. Therefore, in the case where Zr is contained, the Zr content is set to be 0.6% or less. It is preferable that the Zr content be 0.01% or more and 0.6% or less, because the effect described above is realized more effectively with a Zr content of 0.01% or more.
  • the Zr content is more preferably 0.05% or more and 0.4% or less.
  • Cu is a chemical element which is effective for increasing the corrosion resistance of stainless steel.
  • excessive Cu content is not desirable, because it causes a decrease in the performance of an electrolyte membrane of a fuel cell due to increased dissolution of metal ions, and this tendency is significant with a Cu content of more than 1.00%. Therefore, in the case where Cu is contained, the Cu content is set to be 1.00% or less. It is preferable that the Cu content be 0.05% or more and 1.00% or less, because the effect described above is realized more effectively with a Cu content of 0.05% or more.
  • the Cu content is more preferably 0.2% or more and 0.8% or less.
  • Ni is a chemical element which is effective for increasing corrosion resistance of stainless steel.
  • an excessive Ni content of more than 1.00% causes a decrease in corrosion resistance in a transpassive state due to acceleration of transpassive dissolution. Therefore, in the case where Ni is contained, the Ni content is set to be 1.00% or less. It is preferable that the Ni content be 0.05% or more and 1.00% or less, because the effect described above is realized more effectively with a Ni content of 0.05% or more.
  • the Ni content is more preferably 0.2% or more and 0.8% or less.
  • each of V and W may be contained. In order to realize these effects, it is preferable that the contents of V and W be respectively 0.01% or more and 0.01% or more.
  • each of Ca, Mg, REM (Rare Earth Metals) and B may be contained.
  • the contents of Ca, Mg, REM and B be respectively 0.0005% or more, 0.0005% or more, 0.0005% or more and 0.0001% or more.
  • the balance of the chemical composition is Fe and inevitable impurities.
  • an O content be 0.02% or less, a P content be 0.05% or less, a S content be 0.01% or less and a Sn content be 0.5% or less. It is more preferable that the O content be 0.01% or less, the P content be 0.03% or less, the S content be 0.008% or less and the Sn content be 0.3% or less.
  • Mn is detected in a passivation film of ferritic stainless steel. From the result of investigations on the correlation between existence of Mn in a passivation film and contact resistance, it was confirmed that there is a tendency that the contact resistance is high in the case where Mn is observed in the passivation film. Therefore, the amount of Mn becomes small in a film which is obtained by reforming the passivation film by immersing ferritic stainless steel in the solution for the immersion treatment described above. Therefore, it is preferable that preferable range of an atomic ratio Mn/Fe in a passivation film be 0.01 or less.
  • the stainless steel After stainless steel having a chemical composition described above is produced by melting and casting, the the stainless steel is heated up to a temperature of 1100° C. or higher and 1300° C. or lower, then the steel is hot-rolled with a finishing temperature of 700° C. or higher and 1000° C. or lower and a coiling temperature of 400° C. or higher and 700° C. or lower into a hot-rolled steel strip having a thickness of 2.0 mm or more and 5.0 mm or less.
  • the hot-rolled steel strip obtained as described above is annealed at a temperature of 800° C. or higher and 1200° C.
  • the steel strip is pickled, then the steel strip is cold-rolled, then the cold-rolled steel strip is annealed, then, optionally, cold-rolling and annealing are performed repeatedly, and then a cold-rolled strip having a specified thickness is obtained.
  • Pickling may be performed after annealing the cold-rolled steel strip. Thereafter, as a final annealing, bright annealing is performed at a temperature of 700° C. or higher and 1000° C. or lower in an atmosphere containing hydrogen, and then pickling is performed.
  • said solution mainly contains hydrofluoric acid or a liquid mixture of hydrofluoric acid and nitric acid, and in said solution the concentration of hydrofluoric acid [HF] and the concentration of nitric acid [HNO 3 ] are adjusted so as to satisfy the relationship [HF] ⁇ [HNO 3 ], preferably [HF] ⁇ 2.5[HNO 3 ], at a temperature of 50° C. or higher and 70° C. or lower and for a duration of 10 seconds or more and 300 seconds or less. In this case, it is preferable that the concentration of hydrofluoric acid [HF] be 3.0% or more.
  • An electrolytic treatment may be performed in addition to the immersion treatment.
  • the stainless steel according to the present invention is obtained by the method described above.
  • the stainless steel according to the present invention as a separator of a proton-exchange membrane fuel cell, after obtaining a cold-rolled steel strip of foil type having a thickness of 0.003 mm or more and 0.3 mm or less by repeating cold rolling and annealing of a cold-rolled steel strip as described above, bright annealing as described above is performed as final annealing, then stainless steel to be used for a separator of a proton-exchange membrane fuel cell is obtained by further performing pickling in a solution for an immersion treatment as described above, and then a separator of a proton-exchange membrane fuel cell is obtained by putting the stainless steel into a specified final shape.
  • a cell consists of the separators obtained as described above and a solid polymer electrolyte membrane which is placed between the separators, and a proton-exchange fuel cell is obtained by piling many of the obtained cells in series.
  • Stainless steel indicated by No. 3 in Table 1 described below was produced by vacuum melting and casting, and then heated up to a temperature of 1250° C. Subsequently, hot rolling, annealing of the hot-rolled steel strip (850° C. or higher and 1050° C. or lower) and pickling were performed. Then, stainless steel foil having a thickness of 0.3 mm was obtained by further performing cold rolling, annealing of the cold-rolled steel strip (800° C. or higher and 900° C. or lower), pickling and bright annealing.
  • 1 illustrates the relationship between the composition of the liquid and contact resistance with the concentration of nitric acid in a liquid mixture of hydrofluoric acid and nitric acid on the horizontal axis and the concentration of hydrofluoric acid in a liquid mixture of hydrofluoric acid and nitric acid on the vertical axis, indicating the liquid which caused contact resistance 10 m ⁇ cm 2 or less by ⁇ , the liquid which caused contact resistance 20 m ⁇ cm 2 or less by ⁇ and the liquid which caused contact resistance more than 20 m ⁇ cm 2 by ⁇ .
  • contact resistance becomes the target value 20 m ⁇ cm 2 or less by immersing the stainless steel in a solution for an immersion treatment in which the relationship the concentration of hydrofluoric acid [HF] ⁇ the concentration of nitric acid [HNO 3 ] is satisfied (corresponding to the range above the dotted line in FIG. 1 ).
  • contact resistance becomes 10 m ⁇ cm 2 or less, which means there is a further decrease in contact resistance, by immersing the stainless steel in a liquid mixture in which the relationship [HF] ⁇ 2.5[HNO 3 ] is satisfied (corresponding to the range above the dashed line in FIG. 1 ).
  • Steel grades No. 1 through 15 in Table 1 were produced by vacuum melting and casting, and then heated up to a temperature of 1250° C. Subsequently, hot rolling, annealing of the hot-rolled steel strip (850° C. or higher and 1050° C. or lower) and pickling were performed. Then, stainless steel foil having a thickness of 0.3 mm was obtained by further performing cold rolling, annealing of the cold-rolled steel strip (800° C. or higher and 900° C. or lower), pickling and bright annealing.
  • an atomic ratio Mn/Fe was calculated on the basis of the values obtained by dividing peak areas of Fe and Mn by the respective relative sensitivity factors, where the peak areas were determined by subtracting peaks of metallic state from the peak of electron orbit 2p3/2 of Mn corresponding to a binding energy of from 638 eV to 645 eV and the peak of electron orbit 2p3/2 of Fe corresponding to a binding energy of from 709 eV to 713 eV, respectively.
  • Tables 2 and 3 the cases where Mn was not detected are indicated by the value of 0.000 for Mn/Fe.
  • contact resistance remained 20 m ⁇ cm 2 or less even after a endurance test had been performed.
  • the contact resistance of the samples immersed in solution B was smaller than that of the samples immersed in solution A, and the increasing amount of the contact resistance by the endurance test of the former samples are smaller than that of the latter samples. Therefore, it is thought that the smaller the contact resistance before the endurance test is, the smaller the increasing amount of the contact resistance by the endurance test is.
  • the contact resistance of any of the examples of the present invention immersed in solution B was 10 m ⁇ cm 2 Or less before the endurance test. Therefore, it was confirmed that the value of contact resistance before the endurance test becomes more preferable by immersion in solution B in consideration of an increase in contact resistance by the endurance test.
  • the surfaces of the samples having high contact resistance were yellowish when they were observed after the endurance test. It is thought that a passivation film grew or corrosion products were formed by keeping the samples under the condition of high potential.
  • the ferritic stainless steel according to the present invention can be ideally used for a separator of a proton-exchange fuel cell, because the stainless steel suppresses an increase in contact resistance for a long time of power generation despite not having undergone a surface treatment such as plating and is possible to ensure corrosion resistance in a potential range in which Cr exhibits transpassive dissolution.
  • the stainless steel according to the present invention can be used widely not only for a separator of a proton-exchange fuel cell but also for stainless steel electric parts having conductivity.

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US11085120B2 (en) 2017-04-25 2021-08-10 Jfe Steel Corporation Stainless steel sheet for fuel cell separators and production method therefor
US11618967B2 (en) 2017-10-25 2023-04-04 Jfe Steel Corporation Production method for stainless steel sheet for fuel cell separators
US12074348B2 (en) 2019-01-21 2024-08-27 Jfe Steel Corporation Austenitic stainless steel sheet for fuel cell separators and production method therefor

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CN103154292B (zh) 2016-01-20
EP2626440A1 (en) 2013-08-14
TW201231686A (en) 2012-08-01
US20130316262A1 (en) 2013-11-28
JP5768641B2 (ja) 2015-08-26
EP2626440B1 (en) 2019-02-27
KR20130099148A (ko) 2013-09-05
EP2626440A4 (en) 2016-08-03
TWI437104B (zh) 2014-05-11
KR101558276B1 (ko) 2015-10-07
WO2012046879A1 (ja) 2012-04-12

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